CN112853233A - Preparation method of TWIP steel with high strength and high hydrogen embrittlement resistance - Google Patents

Preparation method of TWIP steel with high strength and high hydrogen embrittlement resistance Download PDF

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Publication number
CN112853233A
CN112853233A CN202110021240.XA CN202110021240A CN112853233A CN 112853233 A CN112853233 A CN 112853233A CN 202110021240 A CN202110021240 A CN 202110021240A CN 112853233 A CN112853233 A CN 112853233A
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steel
hydrogen embrittlement
strength
twip steel
twip
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CN202110021240.XA
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Chinese (zh)
Inventor
周成双
方贝
汤旦
张逸青
张�林
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Zhejiang University of Technology ZJUT
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Zhejiang University of Technology ZJUT
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B21J5/002—Hybrid process, e.g. forging following casting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten

Abstract

The invention provides a preparation method of high-strength and hydrogen embrittlement-resistant TWIP steel. And then, cold rolling the obtained steel ingot at a certain temperature in the same direction until the required requirements are met, and processing the steel ingot into a compact product. The method can greatly improve the hydrogen embrittlement resistance of the TWIP steel and meet the requirement of mechanical property, wherein the tensile strength reaches 860MPa, and the total elongation is 68.5%. The invention can solve the problem that the hydrogen embrittlement resistance, the strength and the like of the TWIP steel after rolling can not meet the requirements at the same time, and provides good performance requirements for the TWIP steel in subsequent processing and application.

Description

Preparation method of TWIP steel with high strength and high hydrogen embrittlement resistance
Technical Field
The invention relates to a preparation method of high-strength and hydrogen embrittlement-resistant TWIP steel, and belongs to the technical field of hydrogen embrittlement resistance of steel materials.
Background
Hydrogen is incorporated into the material during fabrication and processing, and hydrogen atoms generally diffuse into the material, thereby reducing the strength and elongation of the material, a phenomenon known as hydrogen embrittlement. When the alloy is prepared and processed in a high-pressure hydrogen environment, the occurrence of hydrogen embrittlement cannot be avoided for metal materials. Some conventional methods for inhibiting hydrogen embrittlement are relatively expensive, complex in process, and the like. The diffusion coefficient of hydrogen in the face-centered cubic (FCC) structure is significantly lower than that of other structures, and therefore, austenitic stainless steels having the face-centered cubic structure are an application choice, but may be transformed into martensite during long-term use, and the martensite itself has relatively strong hydrogen embrittlement sensitivity, and the cost of, for example, 316 austenitic stainless steel is relatively expensive and expensive to manufacture in industry.
The TWIP steel (twin crystal induced plasticity steel) has the excellent characteristics of high strength, high elongation and the like, has good comprehensive performance, and is widely applied to the fields of automobiles, buildings and the like. In the range of 20-50mJ/m of Stacking Fault Energy (SFE)2In the process, martensite phase transformation is not easy to occur, deformation twin crystals are easy to form, the twin crystal boundary obstructs the movement of dislocation, the possibility of dislocation entanglement is reduced, the fatigue crack propagation rate is reduced, and therefore the hydrogen embrittlement resistance of the TWIP steel is improved. The element Mn is used as a stable phase of austenite, the Stacking Fault Energy (SFE) of the TWIP steel can be improved, and a proper amount of Mn is added, so that more twin crystals can be generated in the plastic deformation process. The C element is used as a solid solution strengthening element to form an interstitial solid solution, so that the strength of the TWIP steel can be improved. There are also certain problems with TWIP steels during manufacture, processing and application, such as at high pressure H2How to improve the hydrogen embrittlement resistance and meet the mechanical property requirements and the like under the environment, and the research and the solution of the problems have important theoretical and application values for the development of the TWIP steel.
Aiming at the existing problems, the invention can effectively improve the hydrogen embrittlement resistance of the TWIP steel, improve the strength and fatigue property of the TWIP steel and the like, provides a direction for the production of parts working in a hydrogen environment, and has important significance for subsequent processing and application.
Disclosure of Invention
The invention aims to provide a preparation method of high-strength and high-hydrogen-brittleness-resistant TWIP steel, which adopts a vacuum induction melting method for melting, wherein raw Fe and Ni are firstly added during melting, Mo is added after furnace burden is melted, Cr is added after deoxidation, and Mn is added 3-5 min before tapping. The obtained steel ingot is forged, homogenized, cooled and cold-rolled. Thereby obtaining the performance requirements of high strength, hydrogen embrittlement resistance and the like required by the alloy.
In order to achieve the purpose, the invention adopts the following technical scheme: the high-strength and hydrogen embrittlement-resistant TWIP steel is characterized by comprising, by weight, 20% -25% of Mn, 0.5% -1.5% of C, 8% -12% of Ni, 0.1% -0.6% of Si, 1% -3% of Cr, 0.5% -2% of Mo, and the balance of Fe and unavoidable impurities.
A preparation method of high-strength and hydrogen embrittlement-resistant TWIP steel comprises the following steps:
(1) adding the raw materials in sequence, smelting in a vacuum induction smelting furnace, introducing protective gas argon, smelting, and casting into steel ingots after smelting is finished;
(2) forging the steel ingot obtained in the step (1) at 900-1100 ℃, homogenizing at 1000-1200 ℃ for 2-3 h, and cooling with water;
(3) and (3) cold rolling the steel ingot obtained in the step (2) at the temperature of-40-100 ℃ in the same forging direction, wherein the cold rolling amount is 20% -40%, rolling is carried out for 2-8 times, and the thickness of the rolled steel ingot is 5-10 mm.
Preferably, the flow rate of the protective gas argon introduced in the step (1) is 1-1.5L/min.
Preferably, the forging temperature in the step (2) is 900-1000 ℃, and the homogenization is 2-2.5 h.
Preferably, the cold rolling temperature in the step (3) is-20-60 ℃, the thickness of the cold rolled steel ingot after each deformation is reduced by 3-7% until the initial thickness is reduced by 20-35%, and the thickness of the rolled steel ingot is 6 mm.
And (3) sample testing:
1. in an environment box filled with high-pressure gasMultiple fatigue crack propagation experiments were performed on an Instron8801(100KN) fatigue testing machine. The experiments were all performed at room temperature, and after the samples were mounted, 5MPa of H was added after the air pressure in the chamber had stabilized2And N2And respectively flushing the steel plates into an environment tank for fatigue crack propagation experiments.
2. The Stacking Fault Energy (SFE) was calculated based on an Olson-Cohen thermodynamic model. In addition, the sample was observed with a Transmission Electron Microscope (TEM).
3. Performing a low strain rate tensile test (SSRT) on an Instron8801(100KN) testing machine, before the test, firstly vacuumizing an environmental chamber to ensure that the vacuum degree is about 0.1Pa, then introducing certain argon for replacement, then continuously vacuumizing to 0.1Pa, and introducing 5MPaH2Or N2The experiment is carried out after the air pressure in the box is stable, and the strain rate of the tensile experiment is 10-5s-1。
The invention has the following advantages:
(1) the TWIP steel has excellent comprehensive performance in H2The strength of the TWIP steel can reach 860MPa in the environment, the total elongation reaches 68.5%, and the TWIP steel has the performance characteristics of high strength and high plasticity, meanwhile, the hydrogen embrittlement resistance of the TWIP steel is greatly improved, the requirements on high strength and high hydrogen embrittlement resistance are met, and good performance requirements are provided for the processing of the TWIP steel, particularly the processing in the hydrogen environment.
(2) The uniformity and consistency of the material in the preparation process of the TWIP steel can be ensured, inclusions, oxides and the like can not be generated, the energy consumption is relatively low, and the prepared product has good quality. And the process is simple, the production process is stable, and the operation is easy.
(3) The prepared TWIP steel can be used for manufacturing corresponding important parts in a high-pressure hydrogen environment, and has wide application prospect.
Drawings
FIG. 1 is a TEM image of an example of the present invention without a cold rolling process;
FIG. 2 is a TEM image of an example of the present invention after a cold rolling process;
FIG. 3 is a graph showing the difference between 5MPaN2At fracture site after mechanical polishing in environmentSEM picture;
FIG. 4 is at 5MPaH2SEM image of fracture position after mechanical polishing under environment;
FIG. 5 shows the measured values at 5MPaN2And H2Graph of crack propagation rate for the environmental examples and 316 stainless steel;
FIG. 6 shows examples at 5MPaN2And H2Stress-strain diagram under environment.
Detailed Description
The high-strength and hydrogen embrittlement-resistant TWIP steel comprises, by weight, 20% -25% of Mn, 0.5% -1.5% of C, 8% -12% of Ni, 0.1% -0.6% of Si, 1% -3% of Cr, 0.5% -2% of Mo, and the balance Fe and unavoidable impurities.
The high-strength and hydrogen embrittlement-resistant TWIP steel is smelted by a vacuum induction smelting method, wherein raw Fe and Ni are added firstly during smelting, Mo is added after furnace burden is melted, Cr is added after deoxidation, and Mn is added 3-5 min before tapping.
Example (b):
the TWIP steel comprises the following chemical components in percentage by weight: 25% of Mn, 0.65% of C, 10% of Ni, 0.3% of Si, 1.5% of Cr, 1% of Mo, and the balance of Fe and unavoidable impurities.
In the embodiment, a vacuum induction smelting method is adopted for smelting, raw Fe and Ni are firstly added during smelting, Mo is added after furnace burden is molten, Cr is added after deoxidation, and Mn is added 3-5 min before tapping.
A preparation method of high-strength and hydrogen embrittlement-resistant TWIP steel comprises the following specific steps:
(1) adding the raw materials in sequence, smelting in a vacuum induction smelting furnace, introducing protective gas argon, smelting, wherein the flow of the protective gas argon is 1L/min, and casting into a steel ingot after smelting is finished;
(2) forging the steel ingot obtained in the step (1) at 950 ℃, homogenizing at 1100 ℃ for 2h, and cooling with water;
(3) and (3) cold-rolling the steel ingot obtained in the step (2) at room temperature in the same forging direction, wherein the thickness of the steel ingot is reduced by 5% after each deformation until the initial thickness is reduced by 30%, and the thickness of the steel ingot after rolling is 6 mm.
TEM image analysis of TWIP steel without cold rolling process and cold rolled TWIP steel of this example: examples the black band marks in the drawings of the cold rolled TWIP steel are twins, the width of the twin beam is about 50nm, and no twins are found in TEM images of the non-cold rolled TWIP steel, indicating that twins are generated during deformation. Scanning Electron Microscope (SEM) images of fracture sites after mechanical polishing can be seen: at H2Under the environment, dense twin crystals can be found in part of the crystal grains; in N2The twins found in the environment were fewer in number and very sparse, indicating that hydrogen promoted twinning. In this example, SFE calculated based on Olson-Cohen thermodynamic model was 38.79mJ/m2It is shown that the TWIP steel of the present example is liable to form deformation twins.
This example gives H at 5MPa2And N2The fatigue crack growth rate was compared to 316 stainless steel in ambient. It can be seen that the fatigue crack propagation rate increases with an increase in the stress intensity factor Δ K. H2The fatigue crack propagation rates of the TWIP steel of the embodiment are all lower than that of the 316 stainless steel under the same stress intensity factor delta K in the environment, which shows that the TWIP steel of the embodiment has better hydrogen embrittlement resistance compared with the 316 stainless steel. While at a lower stress intensity factor Δ K, the TWIP steel of this example was at H2And N2The fatigue crack propagation rates under the environment are not very different. This indicates that the present invention is advantageous for improving the hydrogen embrittlement resistance of TWIP steel.
This example also compares with 316 stainless steel in H2And N2The hydrogen embrittlement sensitivity of the TWIP steel at the fatigue crack propagation rate under the stress intensity factor delta K30 with stronger hydrogen embrittlement effect is compared, and the hydrogen embrittlement sensitivity of the TWIP steel is found to be lower than that of 316 stainless steel according to the data result in the table 1. It can be concluded that the TWIP steel of the present invention exhibits good hydrogen embrittlement resistance.
TABLE 1 in N2And H2Fatigue crack growth rate ratio at Δ K30 for the environmental examples versus 316 stainless steel
Fatigue crack propagation rate 316 stainless steel Examples
N2Environment(s) 3.13*10-4 1.48*10-4
H2Environment(s) 1.07*10-3 1.89*10-4
H2/N2 3.42 1.28
This example was subjected to a low strain rate tensile test (SSRT) given in H2And N2Stress-strain curves for environmentally prepared TWIP steels, with simultaneous pair at 30% H2And 30% N2Stress-strain curves obtained from the prepared TWIP steels were compared under ambient conditions. At H2Under the environment, the tensile strength of the TWIP steel reaches 860MPa and the total elongation reaches 68.5 percent, and the tensile strength is N2The difference is not great under the environment.
This embodiment is also as in H2The performance tests of another TWIP steel (chemical components in weight percent: Mn 23%, C0.65%, balance Fe and unavoidable impurities) under the environment were compared, see table 2. It can be seen that the TWIP steel of the present invention not only exhibits excellent hydrogen embrittlement resistance, but also is improved in performance to some extent.
TABLE 2 performance testing comparison of TWIP steels of the examples with another conventional TWIP steel
Experimental Material Yield strength/MPa Tensile strength/MPa Elongation/percent
Examples 328 860 68.5
Comparative example 283 775 51.0
The test results show that the TWIP steel of the invention shows excellent hydrogen embrittlement resistance in H2The total elongation of the TWIP steel can reach 68.5 percent under the environment, the tensile strength reaches 860MPa, and the TWIP steel meets the requirements of high strength and excellent hydrogen embrittlement resistance. The invention is effective, improves the hydrogen embrittlement resistance and meets the requirement of mechanical property.

Claims (6)

1. The high-strength and hydrogen embrittlement-resistant TWIP steel is characterized by comprising, by weight, 20% -25% of Mn, 0.5% -1.5% of C, 8% -12% of Ni, 0.1% -0.6% of Si, 1% -3% of Cr, 0.5% -2% of Mo, and the balance of Fe and unavoidable impurities.
2. The high-strength and hydrogen embrittlement-resistant TWIP steel according to claim 1, wherein the high-strength and hydrogen embrittlement-resistant TWIP steel is melted by adding raw Fe and Ni, adding Mo after melting a burden, adding Cr after deoxidation, and adding Mn 3-5 min before tapping.
3. A method of manufacturing a high strength and hydrogen embrittlement resistant TWIP steel as claimed in claims 1-2, comprising the steps of:
(1) adding the raw materials in sequence, smelting in a vacuum induction smelting furnace, introducing protective gas argon, smelting, and casting into steel ingots after smelting is finished;
(2) forging the steel ingot obtained in the step (1) at 900-1100 ℃, homogenizing at 1000-1200 ℃ for 2-3 h, and cooling with water;
(3) and (3) cold rolling the steel ingot obtained in the step (2) at the temperature of-40-100 ℃ in the same forging direction, wherein the cold rolling amount is 20-40%, rolling is carried out for 2-8 times, and the thickness of the steel ingot after rolling is 5-10 mm.
4. The preparation method of the high-strength and hydrogen embrittlement-resistant TWIP steel according to claim 2, wherein the flow rate of argon gas introduced into the steel in the step (1) is 1-1.5L/min.
5. The method for preparing a TWIP steel with high strength and hydrogen embrittlement resistance according to claim 2, wherein the forging temperature in step (2) is 900-1000 ℃, and the homogenization is 2-2.5 hours.
6. The preparation method of the high-strength and hydrogen embrittlement-resistant TWIP steel according to claim 2, wherein the cold rolling temperature in the step (3) is-20-60 ℃, the thickness of the cold rolled steel is reduced by 3-7% after each deformation until the initial thickness is reduced by 20-35%, and the thickness of the rolled steel ingot is 6 mm.
CN202110021240.XA 2021-01-07 2021-01-07 Preparation method of TWIP steel with high strength and high hydrogen embrittlement resistance Pending CN112853233A (en)

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Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107574377A (en) * 2017-09-07 2018-01-12 北京科技大学 High manganese TWIP steel of a kind of high energy absorbing type based on nanostructured and preparation method thereof
CN109070282A (en) * 2016-05-02 2018-12-21 埃克森美孚研究工程公司 Welding section resistant to corrosion-corrosive potassium steel the pipeline and its manufacturing method increased with step

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109070282A (en) * 2016-05-02 2018-12-21 埃克森美孚研究工程公司 Welding section resistant to corrosion-corrosive potassium steel the pipeline and its manufacturing method increased with step
CN107574377A (en) * 2017-09-07 2018-01-12 北京科技大学 High manganese TWIP steel of a kind of high energy absorbing type based on nanostructured and preparation method thereof

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
（澳）弗瑞: "《金属及合金带材铸轧工 加工、微观组织和特性》", 31 January 2014 *
唐荻等: "《汽车用先进高强板带钢》", 31 October 2016 *

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Application publication date: 20210528